Tailoring of structural, electrical and magnetic properties of BaCo2 W-type hexaferrites by doping with Zr–Mn binary mixtures for useful applications

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Abstract

Single-phase W-type hexaferrite, BaCo2Fe16−2x(ZrMn)xO27 (x=0.0–1.0), has been synthesized by the chemical co-precipitation technique. Mössbauer analysis indicates substitution of Zr ions on tetrahedral (4e and 4fIV) sites and Mn ions on the octahedral ‘4fVI site’ at low-doped concentration when the concentration is increased Mn ions but show preference for the octahedral ‘2b site’. The highest enhancement in the value of the room temperature resistivity of 2.82×109 Ω cm has been obtained by doping with Zr–Mn content of x=0.6. The dissipation factor increases from 6.49×103 to 9.97×103 at 10 kHz with the addition of Zr–Mn dopants. Such materials are potentially suitable for electromagnetic attenuation purposes, for microwave absorption and as radar absorbing material. High values of saturation magnetization (67 emu/g) and remanent magnetization (34.7 emu/g) are obtained for substitution level of x=0.4 making them suitable for data processing devices.

Highlights

► Zirconium ions preference is for fIV sublattice while Mn ions prefer 4fVI and 2b sublattices. ► Room temperature resistivity of up to 2.82×109 Ω cm is obtained for doped hexaferrites. ► High value of saturation magnetization (67.0 emu/g), remanent magnetization (34.7 emu/g) and coercivity (1861 Oe) make doped hexaferrites to be utilized as data processing devices.

Introduction

Ferrites are important magnetic materials that, find its application in almost 70–80% of the electronic materials such as home appliances, communication equipments and data processing devices [1], [2]. Having a high coercivity and moderate magnetization, hexaferrites are valuable from technological point of view. W-type hexaferrites are suitable for competing in the field of magnetism because of their high saturation magnetization as compared to the most widely used other types of ferrites [3], [4], [5], [6], [7]. Furthermore, with large magneto-crystalline anisotropy in easy axis, W-type hexaferrites are applicable for both longitudinal and perpendicular recording media.

Owing to the crystallographic view, the cations with the exception of the Ba2+ ions in W-type ferrites occupy seven non-equivalent sub-lattices, i.e. 12k, 4fVI, 6g, 4f (octahedral coordination), 4e, 4fIV (tetrahedral coordination) and 2d (bipyramidal coordination) [8], [9]. However, there are only five magnetically non-equivalent sub-lattices from magnetic perspective, i.e. 4e and 4fIV that merge into fIV, magnetic sub-lattice while 6g and 4f combine to 2b sub-lattice and called as b magnetic sub-lattice [10]. All these sub-lattices are present in different number of R-blocks (Ba containing layer) and S-blocks (spinel layer) that construct W-type ferrites [11].

In the last few years variations in different properties of ferrites such as cation distribution, electrical resistivity, saturation magnetization, coercivity and remanence, were made possible by substitution of manganese ions. For example, Mn–Zn doped spinel ferrites, synthesized by combinatorial synthesis, show the effect of various additives on the formation of high performance materials by sintering them at lower temperature [12]. Synthesis of Mn–Zn doped spinel ferrites with Fe-poor composition and investigation of their electromagnetic properties found that the measured value of electrical resistivity (105 Ω cm) is significantly higher than that of the Fe-rich Mn–Zn ferrite and the Curie temperature decreases with substitution of diamagnetic Zn ions [13]. Variations in the crystallite sizes were found to be due to Mn substitution in nickel ferrite, which in turn affected the structural and magnetic properties [14].

In the present work, important modification of structural, electrical and magnetic properties of W-type hexaferrites is achieved by doping with a relatively small amount of the transition metals. The modification of the above-mentioned properties is suitable for their applications in various electrical devices employed for industrial and military applications. The chemical co-precipitation technique [15] has been used to synthesize homogeneous nano-crystallites of hexagonal ferrites because of the simplicity of this technique with respect to both composition and morphology.

Section snippets

Materials

The raw materials utilized in the present work are BaCl2·4H2O (Analar 99%), Co(CH3COO)2·4H2O (Merck 99%), Fe(NO3)3·9H2O (Sigma-Aldrich 98%), ZrOCl2·8H2O (BDH 96%), Mn(CH3COO)2·4H2O (Merck 98%), NaOH (Merck 98%) and Na2CO3 (Merck 99%).

Synthesis of BaCo2Fe16O27 nanoparticles

Samples of composition BaCo2Fe16−2x(ZrMn)xO27 (x=0, 0.2, 0.4, 0.6, 0.8 and 1) were prepared by chemical co-precipitation method. For this stoichiometric ratio, the corresponding chemicals were dissolved in distilled water and thoroughly mixed to form a homogeneous

Structural analysis

X-ray diffraction patterns for BaCo2Fe16−2x(ZrMn)xO27 (x=0, 0.2, 0.4, 0.6, 0.8 and 1) hexaferrites along with the standard pattern (00-019-0098) are shown in Fig. 1. Pure W-type hexagonal ferrites are generally obtained by sintering at temperature ≥1273 K but we are able to synthesize a single W-hexaferrite phase at relatively low annealing temperature of 1193 K. The X-ray density (ρx), cell volume (V) and crystallite sizes (D) are calculated using the well-known equations [15], [16], [17] and

Conclusions

Zr–Mn doped BaCo2 W-type hexaferrites with a nominal composition can be synthesized by chemical co-precipitation technique at a temperature of 1153 K that is comparatively much lower for W-type hexaferrites than that reported in literature. The XRD analysis conforms to the single-phase W-type hexaferrite and the SEM images show that the crystallites are more or less coagulated and the grain growth increased with increase in the dopant concentration. The lattice parameters increase with increase

Acknowledgment

Higher education commission of Pakistan (HEC) supported this work.

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